Polyethylene compositions and closures made from them

ABSTRACT

A dual reactor solution process gives high density polyethylene compositions containing a first ethylene copolymer and a second ethylene copolymer and which have good processability, stiffness, and environmental stress crack resistance. The polyethylene compositions are suitable for compression molding or injection molding applications and are particularly useful in the manufacture of caps and closures for bottles.

CROSS REFERENCE TO RELATED PATENT APPLICATION

This application is a continuation of U.S. application Ser. No. 15/460,808, filed on Mar. 16, 2017 which is a continuation of U.S. application Ser. No. 15/152,601, filed on May 12, 2016, now U.S. Pat. No. 9,637,628, which was granted on May 2, 2017 which is a continuation of U.S. application Ser. No. 14/828,962, filed on Aug. 18, 2015, entitled “POLYETHYLENE COMPOSITION AND CLOSURES MADE FROM THEM”, now U.S. Pat. No. 9,371,442, which was granted Jun. 21, 2016, which is a continuation-in-part of U.S. application Ser. No. 14/557,996 filed on Dec. 2, 2014, now U.S. Pat. No. 9,221,966, which was granted Dec. 29, 2015, entitled “POLYETHYLENE COMPOSITIONS AND CLOSURES FOR BOTTLES”, which is herein incorporated by reference in its entirety and which is a continuation of U.S. application Ser. No. 13/601,509, filed on Aug. 31, 2012, now U.S. Pat. No. 8,962,755, which was granted on Feb. 24, 2015, entitled “POLYETHYLENE COMPOSITIONS AND CLOSURES FOR BOTTLES”, which are herein incorporated by reference in their entirety, and which claim priority and the benefit of Canadian Application No. 2,752,407, filed Sep. 19, 2011.

The present invention relates to polyethylene compositions that are useful in the manufacture of molded articles such as closures for bottles.

Polymer compositions useful for molding applications, specifically the manufacture of caps and closures for bottles are well known. Screw closures for example, are typically made from polypropylene (PP) in order to achieve the necessary cap strength, however, an inner liner composed of a soft polymer is required to provide necessary seal properties. The soft inner liner can be made from ethylene/vinyl acetate (EVA), polyvinyl chloride (PVC), butyl rubber or other suitable material. The two-part cap is costly, and single part constructions are preferred to reduce cost.

Accordingly, one-piece closures, such as screw caps have more recently been made from polyethylene resins. The use of high density resin is required if the closures are to have sufficient stiffness, while broader molecular weight distributions are desirable to impart good flow properties and to improve environmental stress crack resistance (ESCR).

Polyethylene blends produced with conventional Ziegler-Natta or Phillips type catalysts systems can be made having suitably high density and ESCR properties, see, for example, WO 00/71615 and U.S. Pat. No. 5,981,664. However, the use of conventional catalyst systems typically produces significant amounts of low molecular weight polymer chains having high comonomer contents, which results in resins having non-ideal organoleptic properties.

Examples of high density multimodal polyethylene blends made using conventional catalyst systems for the manufacture of caps or closures are taught in U.S. Patent Application Publication Nos. 2005/0004315A1; 2005/0267249A1; as well as WO 2006/048253, WO 2006/048254, WO 2007/060007; and EP 2,017,302A1. Further high density, multimodal polyethylene blends made by employing conventional Ziegler-Natta catalysts are disclosed in U.S. Patent Application Publication Nos. 2009/0062463A1; 2009/0198018; 2009/0203848 and in WO 2007/130515, WO 2008/136849 and WO 2010/088265.

In contrast to traditional catalysts, the use of so called single site catalysts (such as “metallocene” and “constrained geometry” catalysts) provides resin having lower catalyst residues and improved organoleptic properties as taught by U.S. Pat. No. 6,806,338. The disclosed resins are suitable for use in molded articles. Further resins comprising metallocene catalyzed components and which are useful for molding applications are described in U.S. Pat. Nos. 7,022,770; 7,307,126; 7,396,878 and 7,396,881 and 7,700,708.

U.S. Patent Application Publication No. 2011/0165357A1 discloses a blend of metallocene catalyzed resins which is suitable for use in pressure resistant pipe applications.

U.S. Patent Application Publication No. 2006/0241256A1 teaches blends formulated from polyethylenes made using a hafnocene catalyst in the slurry phase.

A bimodal resin having a relatively narrow molecular weight distribution and long chain branching is described in U.S. Pat. No. 7,868,106. The resin is made using a bis-indenyl type metallocene catalyst in a dual slurry loop polymerization process and can be used to manufacture caps and closures.

U.S. Pat. No. 6,642,313 discloses multimodal polyethylene resins which are suitable for use in the manufacture of pipes. A dual reactor solution process is used to prepare the resins in the presence of a phosphinimine catalyst.

Narrow molecular weight polyethylene blends comprising a metallocene produced polyethylene component and a Zielger-Natta or metallocene produced polyethylene component are reported in U.S. Pat. No. 7,250,474. The blends can be used in blow molding and injection molding applications such as for example, milk bottles and bottle caps respectively.

In U.S. Pat. No. 8,022,143, we disclosed a resin composition having a good balance of toughness, ESCR, processability, and organoleptic properties for use in the manufacture of caps and closures. The resins were made using a single site catalyst system in a dual reactor solution process, to provide bimodal polyethylene compositions in which comonomer was present in both a high and a low molecular weight component. The disclosed resins had a normal comonomer distribution in that the low molecular weight component had a larger amount of comonomer than did the high molecular weight component. We have now found that by adding more comonomer to the high molecular weight component of these resins, we can improve the ESCR properties. The polyethylene compositions provided by the present invention also have good organoleptic properties, balanced rheological and mechanical properties and are suitable for use in the manufacture of closures for bottles, or containers or pouches.

Provided in one embodiment is a polyethylene composition that can be used in the manufacture of caps and closures for bottles, containers or pouches.

Provided in another embodiment is a polyethylene composition which has an improved ESCR while maintaining low shear viscosity values at high shear rates which is desirable for high-speed injection or compression molding applications.

Embodiments of the invention include caps and closures comprising a polyethylene composition made by a two reactor solution phase process and a single site catalyst. Plaques made from the polyethylene compositions have a good balance of mechanical, processing and organoleptic properties.

Provided in another embodiment is a closure for bottles, containers or pouches, the closure comprising a bimodal polyethylene composition comprising:

-   -   (1) 10 to 70 wt % of a first ethylene copolymer having a melt         index, I₂, of less than 0.4 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 3.0; and a density of         from 0.920 to 0.955 g/cm³; and     -   (2) 90 to 30 wt % of a second ethylene copolymer having a melt         index I₂, of from 100 to 10,000 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 3.0; and a density         higher than the density of the first ethylene copolymer, but         less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio of short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution, M_(w)/M_(n), of from 3 to 11; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.4 to 5.0 g/10 min; an Mz of less than 400,000; a stress exponent of less than 1.50; and an ESCR Condition B (10% IGEPAL) of at least 20 hours.

Provided in another embodiment is a process to prepare a polyethylene composition, the polyethylene composition comprising:

-   -   (1) 10 to 70 wt % of a first ethylene copolymer having a melt         index, I₂, of less than 0.4 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 3.0; and a density of         from 0.920 to 0.955 g/cm³; and     -   (2) 90 to 30 wt % of a second ethylene copolymer having a melt         index I₂, of from 100 to 10,000 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 3.0; and a density         higher than the density of the first ethylene copolymer, but         less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio of short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the polyethylene composition has a molecular weight distribution, M_(w)/M_(n), of from 3 to 11; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.4 to 5.0 g/10 min; an Mz of less than 400,000; a stress exponent of less than 1.50; and an ESCR Condition B (10% IGEPAL) of at least 20 hours;

the process comprising contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least two polymerization reactors.

Provided in another embodiment is a bimodal polyethylene composition comprising:

-   -   (1) 30 to 60 wt % of a first ethylene copolymer having a melt         index, I₂, of less than 0.4 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 2.7; and a density of         from 0.925 to 0.950 g/cm³; and     -   (2) 70 to 40 wt % of a second ethylene copolymer having a melt         index I₂, of from 100 to 10,000 g/10 min; a molecular weight         distribution, M_(w)/M_(n), of less than 2.7; and a density         higher than the density of the first ethylene copolymer, but         less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio of short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution, M_(w)/M_(n), of from 4.0 to 10.0; a density of from 0.949 to 0.957 g/cm³; a melt index I₂, of from 0.4 to 5.0 g/10 min; a comonomer content of less than 0.75 mol % as determined by ¹³C NMR; an Mz of less than 400,000; a stress exponent of less than 1.50; and an ESCR Condition B (10% IGEPAL) of at least 20 hours.

Provided in another embodiment is a closure, said closure comprising a bimodal polyethylene composition comprising:

-   -   (1) 10 to 70 weight percent of a first ethylene copolymer having         a melt index I₂, of less than 0.4 g/10 min; a molecular weight         distribution M_(w)/M_(n), of less than 2.7; and a density of         from 0.920 to 0.955 g/cm³; and     -   (2) 90 to 30 weight percent of a second ethylene copolymer         having a melt index I₂, of from greater than 500 to 20,000 g/10         min; a molecular weight distribution M_(w)/M_(n), of less than         2.7; and a density higher than the density of said first         ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of said second ethylene copolymer is less than 0.037 g/cm³ higher than the density of said first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in said first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in said second ethylene copolymer (SCB2) is greater than 1.0; and wherein said bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 6 to 13; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.2 to 3.0 g/10 min; an Mz of less than 450,000; a stress exponent of less than 1.50, and an ESCR Condition B (10% IGEPAL) of at least 200 hours.

Provided in another embodiment is a process to prepare a polyethylene composition, said polyethylene composition, comprising:

-   -   (1) 10 to 70 weight percent of a first ethylene copolymer having         a melt index I₂, of less than 0.4 g/10 min; a molecular weight         distribution M_(w)/M_(n), of less than 2.7; and a density of         from 0.920 to 0.955 g/cm³; and     -   (2) 90 to 30 weight percent of a second ethylene copolymer         having a melt index I₂, of from greater than 500 to 20,000 g/10         min; a molecular weight distribution M_(w)/M_(n), of less than         2.7; and a density higher than the density of said first         ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of said second ethylene copolymer is less than 0.037 g/cm³ higher than the density of said first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in said first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in said second ethylene copolymer (SCB2) is greater than 1.0; and wherein said bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 6 to 13; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.2 to 3.0 g/10 min; an Mz of less than 450,000; a stress exponent of less than 1.50, and an ESCR Condition B (10% IGEPAL) of at least 200 hours; said process comprising contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin under solution polymerization conditions in at least two polymerization reactors.

Provided in another embodiment is a bimodal polyethylene composition comprising:

-   -   (1) 10 to 70 weight percent of a first ethylene copolymer having         a melt index I₂, of less than 0.4 g/10 min; a molecular weight         distribution M_(w)/M_(n), of less than 2.7; and a density of         from 0.920 to 0.955 g/cm³; and (2) to 30 weight percent of a         second ethylene copolymer having a melt index I₂, of from         greater than 500 to 20,000 g/10 min; a molecular weight         distribution M_(w)/M_(n), of less than 2.7; and a density higher         than the density of said first ethylene copolymer, but less than         0.967 g/cm³;

wherein the density of said second ethylene copolymer is less than 0.037 g/cm³ higher than the density of said first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in said first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in said second ethylene copolymer (SCB2) is greater than 1.0; and wherein said bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 6 to 13; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.2 to 3.0 g/10 min; an Mz of less than 450,000; a stress exponent of less than 1.50, and an ESCR Condition B (10% IGEPAL) of at least 200 hours.

In an embodiment of the invention, the bimodal polyethylene composition has an ESCR Condition B (10% IGEPAL) of at least 350 hours.

In an embodiment of the invention, the bimodal polyethylene composition has an ESCR Condition B (10% IGEPAL) of greater than 400 hours.

In an embodiment of the invention, the bimodal polyethylene composition has a molecular weight distribution, M_(w)/M_(n), of from 8 to 12.

In an embodiment of the invention, the bimodal polyethylene composition has melt index I₂, of from 0.4 to 2.0 g/10 min.

In an embodiment of the invention, the second ethylene copolymer has a melt index I₂ of greater than 650 g/10 min.

In an embodiment of the invention, the second ethylene copolymer has a melt is density of less than 0.965 g/cm³.

In an embodiment of the invention, the bimodal polyethylene composition has a z-average molecular weight distribution, Mz/Mw of less than 4.0

In an embodiment of the invention, the first ethylene copolymer has a density of from 0.925 to 0.950 g/cm³.

In an embodiment of the invention, the bimodal polyethylene composition has a density of from 0.951 to 0.957 g/cm³.

In an embodiment of the invention, the density of the second ethylene copolymer is less than 0.035 g/cm³ higher than the density of the first ethylene copolymer.

In an embodiment of the invention, the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.5.

In an embodiment of the invention, the bimodal polyethylene composition has a composition distribution breadth index (CDBI₂₅) of greater than 55% by weight.

In an embodiment of the invention, the second ethylene copolymer has a melt index, I₂ of from 1,000 to 20,000.

In an embodiment of the invention, the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.5.

In an embodiment of the invention, the bimodal polyethylene composition comprises: from 30 to 60 wt % of the first ethylene copolymer; and from 70 to 40 wt % of the second ethylene copolymer.

In an embodiment of the invention, the bimodal polyethylene composition has a shear viscosity ratio of ≥12.5.

In an embodiment of the invention, the bimodal polyethylene composition has a broadness factor defined as (M_(w)/M_(n))/(M_(z)/M_(w)) of at least 2.75.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 shows a plot of the ESCR in hours (the ESCR B10 for a molded plaque) against the 2% secant flexural modulus (MPa) for selected inventive and comparative polyethylene composition examples.

FIG. 2 shows a plot of the ESCR in hours (the ESCR B10 for a molded plaque) against the shear viscosity ratio (η₁₀/η₁₀₀₀ at 240° C.) for selected inventive and comparative polyethylene composition examples.

FIG. 3 shows a plot of the shear viscosity ratio (η₁₀/η₁₀₀₀ at 240° C.) against the notched Izod Impact Strength (J/m) for selected inventive and comparative polyethylene composition examples.

FIG. 4 shows a plot of the shear viscosity ratio (η₁₀/η₁₀₀₀ at 240° C.) against the 2% secant flexural modulus (MPa) for selected inventive and comparative polyethylene composition examples.

FIG. 5 shows the relationship between the shear thinning index SHI(1,100) and the melt index, I₂ of polyethylene compositions of the current invention.

FIG. 6 shows a gel permeation chromatograph for inventive polyethylene compositions Nos 10-13.

FIG. 7 shows the relationship between the shear thinning index SHI(1,100) and the melt index, I₂ of polyethylene compositions of the current invention (inventive polyethylene composition examples Nos 10-13).

DETAILED DESCRIPTION

The present invention is related to caps and closures for bottles or container or pouches and to the polyethylene compositions used to manufacture them. The polyethylene compositions are composed of at least two ethylene copolymer components: a first ethylene copolymer and a second ethylene copolymer. The polyethylene compositions of the invention have a good balance of processability, toughness, stiffness, environmental stress crack resistance, and organoleptic properties making them ideal materials for use in manufacturing caps and closures for bottles or containers or pouches.

By the term “ethylene copolymer” it is meant that the copolymer comprises both ethylene and at least one alpha-olefin comonomer.

The terms “cap” and “closure” are used interchangeably in the current invention, and both connote any suitably shaped molded article for enclosing, sealing, closing or covering etc., a suitably shaped opening, a suitably molded aperture, an open necked structure or the like used in combination with a container, a bottle, a jar, a pouch and the like.

The terms “homogeneous” or “homogeneously branched polymer” as used herein define homogeneously branched polyethylene which has a relatively narrow composition distribution, as indicated by a relatively high composition distribution breadth index (CDBI₅₀). That is, the comonomer is randomly distributed within a given polymer chain and a substantial portion of the polymer chains have same ethylene/comonomer ratio.

It is well known that metallocene catalysts and other so called “single site catalysts” incorporate comonomer more evenly than traditional Ziegler-Natta catalysts when used for catalytic ethylene copolymerization with alpha olefins. This fact is often demonstrated by measuring the composition distribution breadth index (CDBI₅₀) for corresponding ethylene copolymers. The composition distribution of a polymer can be characterized by the short chain distribution index (SCDI) or composition distribution breadth index (CDBI₅₀). The definition of composition distribution breadth index (CDBI₅₀) can be found in PCT publication WO 93/03093 and U.S. Pat. No. 5,206,075. The CDBI₅₀ is conveniently determined using techniques which isolate polymer fractions based on their solubility (and hence their comonomer content). For example, temperature rising elution fractionation (TREF) as described by Wild et al. J. Poly. Sci., Poly. Phys. Ed. Vol. 20, p 441, 1982 or in U.S. Pat. No. 4,798,081 can be employed. From the weight fraction versus composition distribution curve, the CDBI₅₀ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median. Generally, Ziegler-Natta catalysts produce ethylene copolymers with a CDBI₅₀ of less than about 50 weight %, or less than about 55 weight %, consistent with a heterogeneously branched copolymer. In contrast, metallocenes and other single site catalysts will most often produce ethylene copolymers having a CDBI₅₀ of greater than about 55 weight %, or greater than about 60 weight %, consistent with a homogeneously branched copolymer.

The First Ethylene Copolymer

In an embodiment of the invention, the first ethylene copolymer of the polyethylene composition has a density of from about 0.920 g/cm³ to about 0.955 g/cm³; a melt index, I₂, of less than about 0.4 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight, M_(w), that is greater than the M_(w) of the second ethylene copolymer. In an embodiment of the invention, the weight average molecular weight, M_(w), of the first ethylene copolymer is at least 110,000.

In an embodiment of the invention, the first ethylene copolymer of the polyethylene composition has a density of from about 0.920 g/cm³ to about 0.955 g/cm³; a melt index, I₂, of less than about 0.4 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 2.7 and a weight average molecular weight, M_(w), that is greater than the M_(w) of the second ethylene copolymer.

In an embodiment of the invention, the first ethylene copolymer is a homogeneously branched copolymer.

In an embodiment of the invention, the first ethylene copolymer is made with a single site catalyst, such as for example a phosphinimine catalyst.

In an embodiment of the invention, the comonomer (i.e. alpha-olefin) content in the first ethylene copolymer can be from about 0.05 to about 3.0 mol %. The comonomer content of the first ethylene polymer is determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In embodiments of the invention, the comonomer in the first ethylene copolymer is one or more olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like.

In an embodiment of the invention, the first ethylene copolymer is a copolymer of ethylene and 1-octene.

In an embodiment of the invention, the short chain branching in the first ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB1/1000Cs). In further embodiments of the invention, the short chain branching in the first ethylene copolymer can be from 0.5 to 15, or from 0.5 to 12, or from 0.5 to 10, or from 0.75 to 15, or from 0.75 to 12, or from 0.75 to 10, or from 1.0 to 10, or from 1.0 to 8.0, or from 1.0 to 5, or from 1.0 to 3 branches per thousand carbon atoms (SCB1/1000Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The number of short chain branches in the first ethylene copolymer is determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the invention, the comonomer content in the first ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.01 mol %) to the comonomer content of the second ethylene copolymer (as reported, for example, in mol %).

In an embodiment of the invention, the comonomer content in the first ethylene copolymer, is greater than comonomer content of the second ethylene copolymer (as reported for example in mol %).

In an embodiment of the invention, the amount of short chain branching in the first ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.05 SCB/1000Cs) to the amount of short chain branching in the second ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In an embodiment of the invention, the amount of short chain branching in the first ethylene copolymer is greater than the amount of short chain branching in the second ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In an embodiment of the invention, the melt index, I₂ of the first ethylene copolymer is less than 0.4 g/10 min. The melt index of the first ethylene copolymer can in an embodiment of the invention be above 0.01, but below 0.4 g/10 min. In further embodiments of the invention, the melt index, I₂ of the first ethylene copolymer will be from 0.01 to 0.40 g/10 min, or from 0.01 to 0.30 g/10 min, or from 0.01 to 0.25 g/10 min, or from 0.01 to 0.20 g/10 min, or from 0.01 to 0.10 g/10 min.

In an embodiment of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 110,000 to about 300,000 (g/mol). In another embodiment of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 110,000 to about 275,000 or from about 110,000 to about 250,000. In another embodiment of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of greater than about 110,000 to less than about 250,000. In further embodiments of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 125,000 to about 225,000, or from about 135,000 to about 200,000. In embodiments of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 125,000 to about 275,000, or from about 125,000 to about 250,000, or from about 150,000 to about 275,000, or from about 150,000 to about 250,000, or from about 175,000 to about 250,000. In embodiments of the invention, the first ethylene copolymer has a M_(w) of greater than 110,000, or greater than 125,000, or greater than 150,000, or greater than 175,000. In embodiments of the invention the first ethylene copolymer has a M_(w) of greater than 110,000, or greater than 125,000, or greater than 150,000, or greater than 175,000 while at the same time being lower than 275,000, or 250,000.

In embodiments of the invention, the density of the first ethylene copolymer is from 0.920 to 0.955 g/cm³ or can be a narrower range within this range. For example, in further embodiments of the invention, the density of the first ethylene copolymer can be from 0.925 to 0.955 g/cm³, or from 0.925 to 0.950 g/cm³, or from 0.925 to 0.945 g/cm³, or from 0.925 to 0.940 g/cm³, or from 0.925 to 0.935 g/cm³, or from 0.923 to 0.945 g/cm³, or from 0.923 to 0.940 g/cm³, or from 0.923 to 0.935 g/cm³, or from 0.927 to 0.945 g/cm³, or from 0.927 to 0.940 g/cm³, or from 0.927 to 0.935 g/cm³.

In an embodiments of the invention, the first ethylene copolymer has a molecular weight distribution M_(w)/M_(n) of <3.0, or ≤2.7, or <2.7, or ≤2.5, or <2.5, or ≤2.3, or from 1.8 to 2.3.

The M_(w)/M_(n) value of the first ethylene copolymer can in an embodiment of the invention be estimated by a de-covolution of a GPC profile obtained for a bimodal polyethylene composition of which the first ethylene copolymer is a component.

The density and the melt index, I₂, of the first ethylene copolymer can be estimated from GPC (gel permeation chromatography) and GPC-FTIR (gel permeation chromatography with Fourier transform infra-red detection) experiments and deconvolutions carried out on the bimodal polyethylene composition (see the Examples section).

In an embodiment of the invention, the first ethylene copolymer of the polyethylene composition is a homogeneously branched ethylene copolymer having a weight average molecular weight, M_(w), of at least 110,000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density of from 0.920 to 0.948 g/cm³.

In an embodiment of the present invention, the first ethylene copolymer is homogeneously branched ethylene copolymer and has a CDBI₅₀ of greater than about 50%, or greater than about 55% by weight. In further embodiments of the invention, the first ethylene copolymer has a CDBI of greater than about 60%, or greater than about 65%, or greater than about 70%, or greater than about 75%, or greater than about 80% by weight.

In an embodiment of the invention, the first ethylene copolymer can comprise from 10 to 70 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from 20 to 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from 30 to 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from 40 to 50 weight percent (wt %) of the total weight of the first and second ethylene copolymers.

The Second Ethylene Copolymer

In an embodiment of the invention, the second ethylene copolymer of the polyethylene composition has a density below 0.967 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index, I₂, of from about 100 to 10,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer. In an embodiment of the invention, the weight average molecular weight, M_(w) of the second ethylene copolymer will be below 45,000.

In an embodiment of the invention, the second ethylene copolymer of the polyethylene composition has a density below 0.967 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index, I₂, of from about 500 to about 20,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 2.7, and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer.

In an embodiment of the invention, the second ethylene copolymer is homogeneously branched copolymer.

In an embodiment of the invention, the second ethylene copolymer is made with a single site catalyst, such as for example a phosphinimine catalyst.

In an embodiment of the invention, the comonomer content in the second ethylene copolymer can be from about 0.05 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods. The comonomer content of the second ethylene polymer can also be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the invention, the comonomer content in the second ethylene copolymer can be from about 0.01 to about 3 mol %, or from about 0.03 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods. The comonomer content of the second ethylene polymer can also be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the invention, the comonomer in the second ethylene copolymer is one or more alpha olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like.

In an embodiment of the invention, the second ethylene copolymer is a copolymer of ethylene and 1-octene.

In an embodiment of the invention, the short chain branching in the second ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB2/1000Cs). In further embodiments of the invention, the short chain branching in the second ethylene copolymer can be from 0.25 to 12, or from 0.25 to 8, or from 0.25 to 5, or from 0.25 to 3, or from 0.25 to 2 branches per thousand carbon atoms (SCB2/1000Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The number of short chain branches in the second ethylene copolymer can be measured by ¹³C NMR, or FTIR or GPC-FTIR methods. Alternatively, the number of short chain branches in the second ethylene copolymer can be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section). The comonomer is one or more suitable alpha olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like, with 1-octene being preferred.

In an embodiment of the invention, the short chain branching in the second ethylene copolymer can be from about 0.05 to about 12 short chain branches per thousand carbon atoms (SCB1/1000Cs). In further embodiments of the invention, the short chain branching in the second ethylene copolymer can be from 0.05 to 7.5, or from 0.05 to 5.0, or from 0.05 to 2.5, or from 0.05 to 1.5, or from 0.1 to 12, or from 0.1 to 10, or from 0.1 to 7.5, or from 0.1 to 5.0, or from 0.1 to 2.5, or from 0.1 to 2.0, or from 0.1 to 1.0 branches per thousand carbon atoms (SCB1/1000Cs).

In an embodiment of the invention, the comonomer content in the second ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.01 mol %) to the comonomer content of the first ethylene copolymer (as reported, for example, in mol %).

In an embodiment of the invention, the comonomer content in the second ethylene copolymer is less than the comonomer content of the first ethylene copolymer (as reported for example in mol %).

In an embodiment of the invention, the amount of short chain branching in the second ethylene copolymer is substantially similar or approximately equal (e.g. within about ±0.05 SCB/1000C) to the amount of short chain branching in the first ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In an embodiment of the invention, the amount of short chain branching in the second ethylene copolymer is less than the amount of short chain branching in the first ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In an embodiment of the present invention, the density of the second ethylene copolymer is less than 0.967 g/cm³. The density of the second ethylene copolymer in another embodiment of the invention is less than 0.966 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.965 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.964 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.963 g/cm³. In another embodiment of the invention; the density of the second ethylene copolymer is less than 0.962 g/cm³.

In an embodiment of the present invention, the density of the second ethylene copolymer, is higher than the density of the first ethylene copolymer, but is less than 0.967 g/cm³. The density of the second ethylene copolymer in another embodiment of the invention is higher than the density of the first ethylene copolymer, but is less than 0.966 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is, higher than the density of the first ethylene copolymer, but is less than 0.965 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.964 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.963 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.962 g/cm³.

In an embodiment of the invention, the density of the second ethylene copolymer is from 0.952 to 0.967 g/cm³ or can be a narrower range within this range. For example, the density of the second ethylene copolymer may in embodiments of the invention be from 0.952 to 0.966 g/cm³, 0.952 to 0.965 g/cm³, or from 0.952 to 0.964 g/cm³, or from 0.952 to 0.963 g/cm³, or from 0.954 to 0.963 g/cm³, or from 0.954 to 0.964 g/cm³, or from 0.956 to 0.964 g/cm³, or from 0.952 to less than 0.965 g/cm³, or from 0.954 to less than 0.965 g/cm³.

In an embodiment of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of less than 25,000. In another embodiment of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 7,500 to about 23,000. In further embodiments of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 22,000, or from about 10,000 to about 17,500, or from about 7,500 to about 17,500. In still further embodiments of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 3,500 to about 25,000, or from about 5,000 to about 20,000, or from about 7,500 to about 17,500, or from about 5,000 to about 15,000, or from about 5,000 to about 17,500, or from about 7,500 to about 15,000 or from about 7,500 to about 12,500. In further embodiments of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 22,000, or from about 10,000 to about 17,500, or from about 7,500 to 17,500.

In embodiments of the invention, the second ethylene copolymer has a molecular weight distribution, M_(w)/M_(n) of <3.0, or ≤2.7, or <2.7, or ≤2.5, or <2.5, or ≤2.3, or from 1.8 to 2.3.

The M_(w)/M_(n) value of the second ethylene copolymer can in an embodiment of the invention be estimated by a de-convolution of a GPC profile obtained for a bimodal polyethylene composition of which the first ethylene copolymer is a component.

In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 20 to 10,000 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 100 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1000 to 7000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1200 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1500 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 1500, but less than 7000 g/10 min.

In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 250 to 20,000 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 500 to 20,000 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from greater than 750 to 20,000 g/10 min. In further embodiments of the invention, the melt index I₂ of the second ethylene copolymer can be from 1000 to 20,000 g/10 min, or from 1,500 to 20,000 g/10 min, or from 250 to 15,000 g/10 min, or from 250 to 10,000 g/10 min or from 500 to 17,500 g/10 min, or from 500 to 15,000 g/10 min, or from 1,500 to 15,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1200 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1500 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 1500, but less than 7000 g/10 min.

In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 200 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 250 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 500 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 650 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1000 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1200 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1500 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1750 g/10 min.

The density and the melt index, I₂, of the second ethylene copolymer can be estimated from GPC and GPC-FTIR experiments and deconvolutions carried out on a bimodal polyethylene composition (see the below Examples section).

In an embodiment of the invention, the second ethylene copolymer of the polyethylene composition is a homogeneous ethylene copolymer having a weight average molecular weight, M_(w), of at most 45000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density higher than the density of said first ethylene copolymer, but less than 0.967 g/cm³.

In an embodiment of the present invention, the second ethylene copolymer is homogeneously branched ethylene copolymer and has a CDBI₅₀ of greater than about 50 weight %, or of greater than about 55 weight %. In further embodiments of the invention, the second ethylene copolymer has a CDBI₅₀ of greater than about 60 weight %, or greater than about 65 weight %, or greater than about 70 weight %, or greater than about 75 weight %, or greater than about 80 weight %.

In an embodiment of the invention, the second ethylene copolymer can comprise from 90 to 30 weight % (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from 80 to 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from 70 to 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from 60 to 50 wt % of the total weight of the first and second ethylene copolymers.

In the present invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.037 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.036 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.035 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.034 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.033 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.032 g/cm³ higher than the density of the first ethylene copolymer. In another embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.031 g/cm³ higher than the density of the first ethylene copolymer. In still another embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.030 g/cm³ higher than the density of the first ethylene copolymer.

In embodiments of the invention, the 12 of the second ethylene copolymer is at least 100 times, or at least 1000 times, or at least 10,000, or at least 50,000 times the 12 of the first ethylene copolymer.

The Polyethylene Composition

The polyethylene composition of this invention has a broad, bimodal or multimodal molecular weight distribution. Minimally, the polyethylene composition will contain a first ethylene copolymer and a second ethylene copolymer (as defined above) which are of different weight average molecular weight (M_(w)) and/or melt index, I₂.

In the present invention, the polyethylene composition will minimally comprise a first ethylene copolymer and a second ethylene copolymer (as defined above) and the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (i.e., SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (i.e., SCB2) will be greater than 0.5 (i.e., SCB1/SCB2>0.5).

In an embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 0.60. In an embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 0.75. In another embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.0. In another embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at greater than 1.0. In yet another embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.25. In still further embodiments of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.5, or at least 2.0, or at least 2.5, or at least 3.0, or at least 3.5, or at least 4.0 or at least 4.5.

In an embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be greater than 0.5, but less than 1.0.

In embodiments of the invention, the ratio (SCB1/SCB2) of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from 1.0 to 12.0, or from 1.0 to 10, or from 1.0 to 7.0, or from 1.0 to 5.0, or from 1.0 to 3.0.

In embodiments of the invention, the ratio (SCB1/SCB2) of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from 1.0 to 15.0, or from 2.0 to 12.0, or from 2.5 to 12.0, or from 3.0 to 12.0, or from 3.5 to 12.0.

In an embodiment of the invention, the polyethylene composition has a bimodal molecular weight distribution. In the current invention, the term “bimodal” means that the polyethylene composition comprises at least two components, one of which has a lower weight average molecular weight and a higher density and another of which has a higher weight average molecular weight and a lower density. Typically, a bimodal or multimodal polyethylene composition can be identified by using gel permeation chromatography (GPC). Generally, the GPC chromatograph will exhibit two or more component ethylene copolymers, where the number of component ethylene copolymers corresponds to the number of discernible peaks. One or more component ethylene copolymers may also exist as a hump, shoulder or tail relative to the molecular weight distribution of the other ethylene copolymer component.

In an embodiment of the invention, the polyethylene composition has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.4 to about 5.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 3 to about 11, a Z-average molecular weight, M_(z) of less than 400,000 a stress exponent of less than 1.50 and an ESCR Condition B at 10% of at least 20 hours.

In an embodiment of the invention, the polyethylene composition of the current invention has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.2 to about 5.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 6 to about 13, a Z-average molecular weight M_(z) of less than 450,000, a stress exponent of less than 1.50 and an ESCR Condition B at 10% of at least 200 hours.

In embodiments of the invention, the polyethylene composition has a comonomer content of less than 0.75 mol %, or less than 0.70 mol %, or less than 0.65 mol %, or less than 0.60 mol %, or less than 0.55 mol % as measured by FTIR or ¹³C NMR methods, with ¹³C NMR being preferred, where the comonomer is one or more suitable alpha olefins such as but not limited to 1-butene, 1-hexene, 1-octene and the like. In an embodiment of the invention, the polyethylene composition has a comonomer content of from 0.1 to 0.75 mol %, or from 0.20 to 0.55 mol %, or from 0.25 to 0.50 mol %.

In the present invention, the polyethylene composition has a density of at least 0.949 g/cm³. In further embodiments of the invention, the polyethylene composition has a density of >0.949 g/cm³, or ≥0.950 g/cm³, or >0.950 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.949 to 0.960 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.949 to 0.959 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.949 to 0.957 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.949 to 0.956 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.949 to 0.955 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.950 to 0.955 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.951 to 0.957 g/cm³.

In an embodiment of the current invention, the polyethylene composition has a density in the range of from 0.951 to 0.955 g/cm³.

In an embodiment of the invention, the polyethylene composition has a melt index, I₂, of between 0.4 and 5.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) and including narrower ranges within this range. For example, in further embodiments of the invention, the polyethylene composition has a melt index, I₂, of from 0.5 to 5.0 g 10 min, or from 0.4 to 3.5 g/10 min, or from 0.4 to 3.0 g/10 min, or from 0.4 to 2.5 g/10 min, or from 0.4 to 2.0 g/10 min, or from 0.5 to 3.5 g/10 min, or from 0.5 to 3.0 g/10 min, or from 1.0 to 3.0 g/10 min, or from about 1.0 to about 2.0 g/10 min, or from more than 0.5 to less than 2.0 g/10 min.

In an embodiment of the invention, the polyethylene composition has a melt index, I₂, of between 0.1 and 5.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) and including narrower ranges within this range. For example, in further embodiments of the invention, the polyethylene composition has a melt index, I₂, of from 0.2 to 5.0 g/10 min, or from 0.3 to 4.0 g/10 min, or from 0.3 to 3.5 g/10 min, or from 0.3 to 3.0 g/10 min, or from 0.2 to 3.5 g/10 min, or from 0.2 to 3.0 g/10 min, or from 0.1 to 2.5 g/10 min, or from 0.1 to 2.0 g/10 min.

In an embodiment of the invention, the polyethylene composition has a melt index I₅ of at least 1.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In another embodiment of the invention, the polyethylene composition has a melt index, I₅, of greater than about 1.1 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In still further embodiments of the invention, the polyethylene composition has a melt index I₅ of from about 1.0 to about 10.0 g/10 min, or from about 2.0 to about 8.0 g/10 min, or from about 1.0 to about 5.0 g/10 min, or from about 1.5 to about 6.5 g/10 min, or from about 4.0 to about 7.0 g/10 min, or from about 3.0 to about 6.5 g/10 min.

In an embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁ of at least 25 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 21 kg weight). In another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 30 g/10 min. In yet another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 35 g/10 min. In still another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 40 g/10 min. In still another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 50 g/10 min. In still another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 60 g/10 min. In still another embodiment of the invention, the polyethylene composition has a high load melt index, I₂₁, of greater than about 75 g/10 min.

In an embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 200 to 1500. In another embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 400 to 1300. In yet another embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 600 to 1200.

In an embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 500 to 5000. In another embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 750 to 4500. In yet another embodiment of the invention, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the polyethylene composition is from 1000 to 4000.

In an embodiment of the invention, the polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere between from about 1 to about 10 kPa which is between 1,000 to 25,000 Pa·s. In an embodiment of the invention, the polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere from about 1 to about 10 kPa which is between 1,000 and 10,000 Pa·s.

In an embodiment of the invention, the polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere between from about 1 to about 10 kPa which is between 1,000 and 25,000 Pa·s. In an embodiment of the invention, the polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere from about 1 to about 10 kPa which is between 1,000 and 10,000 Pa·s, or between 1,000 and 15,000 Pa·s, or from 3,000 to 12,500 Pa·s.

In an embodiment of the invention, the polyethylene composition has a number average molecular weight, M_(n), of below about 30,000. In another embodiment of the invention, the polyethylene composition has a number average molecular weight, M_(n), of below about 20,000 or below about 17,500. In further embodiments of the invention, the polyethylene composition has a number average molecular weight, M_(n), of from about 5,000 to 25,000, or from about 5,000 to 20,000, or from about 7,000 to about 15,000.

In embodiments of the invention, the polyethylene composition has a weight average molecular weight, M_(w), of from about 60,000 to about 200,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the invention, the polyethylene composition has a weight average molecular weight, M_(w), of from about 65,000 to 175,000, or from about 65,000 to about 150,000, or from about 65,000 to about 140,000.

In an embodiment of the invention, the polyethylene composition has a z-average molecular weight, M_(z), of less than 450,000.

In embodiments of the invention, the polyethylene composition has a z-average molecular weight, M_(z) of from 250,000 to 450,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the invention, the polyethylene composition has a z-average molecular weight, M_(z), of from 250,000 to 425,000, or from 275,000 to 425,000, or from 250,000 to below 450,000, or from 250,000 to 410,000.

In embodiments of the present invention, the polyethylene composition has a molecular weight distribution M_(w)/M_(n) of from 3 to 11 or a narrower range within this range. For example, in further embodiments of the invention, the polyethylene composition has a M_(w)/M_(n) of from 4.0 to 10.0, or from 4.0 to 9.0 or from 5.0 to 10.0, or from 5.0 to 9.0, or from 4.5 to 10.0, or from 4.5 to 9.5, or from 4.5 to 9.0, or from 4.5 to 8.5, or from 5.0 to 8.5.

In embodiments of the present invention, the polyethylene composition has a molecular weight distribution M_(w)/M_(n) of from 6 to 13 or a narrower range within this range. For example, in further embodiments of the invention, the polyethylene composition has a M_(w)/M_(n) of from 7.0 to 12.0, or from 8.0 to 12.0, or from 8.5 to 12.0, or from 9.0 to 12.0, or from 9.0, to 12.5 or from 8.5 to 12.5.

In embodiments of the invention, the polyethylene composition has a ratio of Z-average molecular weight to weight average molecular weight (M_(z)/M_(w)) of from 2.0 to 5.0, or from 2.25 to 4.75, or from 2.25 to 4.5, or from 2.5 to 4.25, or from 2.75 to 4.0, or from 2.75 to 3.75, or between 3.0 and 4.0.

In embodiments of the invention, the polyethylene composition has a ratio of Z-average molecular weight to weight average molecular weight (M_(z)/M_(w)) of less than 5.0, or less than 4.5, or less than 4.0, or less than 3.5.

In an embodiment of the invention, the polyethylene composition has a broadness factor defined as (M_(w)/M_(n))/(M_(z)/M_(w)) of at least 2.70, or at least 2.75, or at least 2.8, or at least 2.85, or at least 2.90, or at least 2.95, or at least 3.00, or at least 3.05.

In embodiments of the invention, the polyethylene composition has a melt flow ratio defined as I₂₁/I₂ of >40, or ≥45, or ≥50, or ≥60, or ≥65. In a further embodiment of the invention, the polyethylene composition has a melt flow ratio I₂₁/I₂ of from about 40 to about 100, and including narrower ranges within this range. For example, the polyethylene composition may have a melt flow ratio I₂₁/I₂ of from about 45 to about 90, or from about 45 to about 80, or from about 45 to about 75, or from about 45 to about 70, or from about 50 to about 90, or from about 50 to about 80, or from about 50 to about 75, or from about 50 to about 70.

In an embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 30. In another embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 25. In another embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 20.

In an embodiment of the invention, the polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than about 10 (Pa·s). In further embodiments of the invention, the polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than 7.5 Pa·s, or less than 6.0 Pa·s.

In an embodiment of the invention, the polyethylene composition has a hexane extractables level of below 0.55 wt %.

In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.75 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.65 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.55 mol % as determined by ¹³C NMR.

In an embodiment of the invention, the shear viscosity ratio, SVR_((10,1000)) at 240° C. of the polyethylene composition can be from about 4.0 to 25, or from 4.0 to 20, or from 4.0 to 17. The shear viscosity ratio SVR_((10,1000)) is determined by taking the ratio of shear viscosity at shear rate of 10 s⁻¹ and shear viscosity at shear rate of 1000 s⁻¹ as measured with a capillary rheometer at constant temperature (e.g. 240° C.), and a die with L/D ratio of 20 and diameter of 0.06″. Without wishing to be bound by theory, the higher the value for the shear viscosity ratio, the easier the polyethylene composition is to be processed on a converting equipment for caps and closures.

In embodiments of the invention, the polyethylene composition has a shear viscosity ratio (η₁₀/η₁₀₀₀ at 240° C.) of ≥12.0, ≥12.5, or ≥13.0, or ≥13.5, or ≥14.0, or ≥14.5, or ≥15.0, or ≥17.5, or ≥20.0. The “shear viscosity ratio” is used herein as a means to describe the relative processability of a polyethylene composition.

In further embodiments of the invention, the shear viscosity ratio, SVR_((10,1000)) at 240° C. of the polyethylene composition is from 10.0 to 30, or from 12.0 to 30, or from 12.0 to 27:5, or from 12.0 to 25, or from 12.5 to 30, or from 12.5 to 27.5, or from 12.5 to 25.

1n an embodiment of the invention, the shear thinning index, SHI_((1,100)) of the polyethylene composition is less than about 10; in another embodiment the SHI_((1,100)) will be less than about 7. The shear thinning index (SHI), was calculated using dynamic mechanical analysis (DMA) frequency sweep methods as disclosed in PCT applications WO 20061048253 and WO 2006/048254. The SHI value is obtained by calculating the complex viscosities η*(1) and η* (100) at a constant shear stress of 1 kPa (G*) and 100 kPa (G*), respectively.

In an embodiment of the invention, the SHI_((1,100)) of the polyethylene composition satisfies the equation: SHI_((1,100))<−10.58 (log I₂ of polyethylene composition in g/10 min)/(g/10 min)+12.94. In another embodiment of the invention, the SHI_((1,100)) of the polyethylene composition satisfies the equation: SHI(1,100)<−5.5(log I ₂ of the polyethylene composition in g/10 min)/(g/10 min)+9.66.

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 20 hours, or at least 60 hours, or at least 80 hours, or at least 120 hours, or at least 150 hours, or from 60 to 400 hours, or from 100 to 250 hours, or from 60 to 250 hours as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 200 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 250 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 300 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 350 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 400 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 200 to 1500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 200 to 1250 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 300 to 1500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the invention, the polyethylene composition or a molded article (or plaque) made from the polyethylene composition has a notched Izod impact strength of at least 60 J/m, or at least 70 J/m, or at least 80 J/m, or at least 90 J/m, or at least 100 J/m as measured according to ASTM D256.

In an embodiment of the invention the polyethylene composition of the current invention has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.5 to 3.0 g/10 min; a molecular weight distribution of from 4.0 to 10.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m, and an ESCR B at 10% of at least 20 hours.

In an embodiment of the invention the polyethylene composition of the current invention has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.5 to 3.0 g/10 min; a molecular weight distribution of from 4.5 to 9.5; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 7 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m and an ESCR B at 10% of at least 80 hours.

In an embodiment of the invention the polyethylene composition of the current invention has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.2 to 3.0 g/10 min; a molecular weight distribution of from 6.0 to 13.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m, and an ESCR B at 10% of at least 200 hours.

In embodiments of the invention, the polyethylene composition has a 2% secant flexural modulus in megapascals (MPa) of greater than about 750, or greater than about 850, or greater than about 1000, or from about 750 to about 1600, or from about 750 to about 1250, or from about 850 to about 1150. In some embodiments the polyethylene composition further comprises a nucleating agent which increases the 2% secant flexural modulus in megapascals (MPa) to above these ranges to for example from more than about 1000 and up to about 1600. Without wishing to be bound by theory, the 2% secant flexural modulus is a measure of polymer stiffness. The higher the 2% secant flexural modulus, the higher the polymer stiffness.

In an embodiment of the invention the polyethylene composition of the current invention has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.2 to 3.0 g/10 min; a molecular weight distribution of from 7.0 to 12.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 7 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m and an ESCR B at 10% of at least 200 hours.

In an embodiment of the invention, the polyethylene composition has a stress exponent, defined as Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16], which is ≤1.50. In further embodiments of the invention the polyethylene composition has a stress exponent, Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16] of less than 1.50, or less than 1.48, or less than 1.45, or less than 1.43, or less than 1.40.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI₅₀), as determined by temperature elution fractionation (TREF), of ≥60 weight %. In further embodiments of the invention, the polyethylene composition will have a CDBI₅₀ of greater than 65 weight %, or greater than 70 weight %, or greater than 75 weight %, or greater than 80 weight %.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI₂₅), as determined by temperature elution fractionation (TREF), of ≥50 weight %. In further embodiments of the invention, the polyethylene composition will have a CDBI₂₅ of greater than 55 weight %, or greater than 60 weight %, or greater than 65 weight %, or greater than 70 weight %.

The polyethylene composition of this invention can be made using any conventional blending method such as but not limited to physical blending and in-situ blending by polymerization in multi reactor systems. For example, it is possible to perform the mixing of the first ethylene copolymer with the second ethylene copolymer by molten mixing of the two preformed polymers. Preferred are processes in which the first and second ethylene copolymers are prepared in at least two sequential polymerization stages, however, both in-series and in-parallel reactor process are contemplated for use in the current invention. If the at least two reactors are configured in parallel, comonomer addition to each reactor makes an ethylene copolymer in each reactor. If the at least two reactors are configured in series, comonomer may be added to at least the first reactor, and unreacted comonomer can flow into later reactors to make an ethylene copolymer in each reactor. Alternatively, if the at least two reactors are configured in series, comonomer may be added to each reactor, to make an ethylene copolymer in each reactor. Gas phase, slurry phase or solution phase reactor systems may be used, with solution phase reactor systems being preferred.

In an embodiment of the current invention, a dual reactor solution process is used as has been described in for example U.S. Pat. No. 6,372,864 and U.S. Patent Publication Application No. 20060247373A1 which are incorporated herein by reference.

Homogeneously branched ethylene copolymers can be prepared using any catalyst capable of producing homogeneous branching. Generally, the catalysts will be based on a group 4 metal having at least one cyclopentadienyl ligand that is well known in the art. Examples of such catalysts which include metallocenes, constrained geometry catalysts and phosphinimine catalysts are typically used in combination with activators selected from methylaluminoxanes, boranes or ionic borate salts and are further described in U.S. Pat. Nos. 3,645,992; 5,324,800; 5,064,802; 5,055,438; 6,689,847; 6,114,481 and 6,063,879. Such catalysts may also be referred to as “single site catalysts” to distinguish them from traditional Ziegler-Natta or Phillips catalysts which are also well known in the art. In general, single site catalysts produce ethylene copolymers having a molecular weight distribution (M_(w)/M_(n)) of less than about 3.0 and a composition distribution breadth index (CDBI₅₀) of greater than about 50% by weight.

In an embodiment of the current invention, homogeneously branched ethylene polymers are prepared using an organometallic complex of a group 3, 4 or 5 metal that is further characterized as having a phosphinimine ligand. Such catalysts are known generally as phosphinimine catalysts. Some non-limiting examples of phosphinimine catalysts can be found in U.S. Pat. Nos. 6,342,463; 6,235,672; 6,372,864; 6,984,695; 6,063,879; 6,777,509 and 6,277,931 all of which are incorporated by reference herein.

Some non-limiting examples of metallocene catalysts can be found in U.S. Pat. Nos. 4,808,561; 4,701,432; 4,937,301; 5,324,800; 5,633,394; 4,935,397; 6,002,033 and 6,489,413, which are incorporated herein by reference. Some non-limiting examples of constrained geometry catalysts can be found in U.S. Pat. Nos. 5,057,475; 5,096,867; 5,064,802; 5,132,380; 5,703,187 and 6,034,021, all of which are incorporated by reference herein in their entirety.

In an embodiment of the invention, use of a single site catalyst that does not produce long chain branching (LCB) is preferred. Without wishing to be bound by any single theory, long chain branching can increase viscosity at low shear rates, thereby negatively impacting cycle times during the manufacture of caps and closures, such as during the process of compression molding. Long chain branching may be determined using ¹³C NMR methods and may be quantitatively assessed using the method disclosed by Randall in Rev. Macromol. Chem. Phys. C29 (2 and 3), p. 285.

In an embodiment of the invention, the polyethylene composition will contain fewer than 0.3 long chain branches per 1000 carbon atoms. In another embodiment of the invention, the polyethylene composition will contain fewer than 0.01 long chain branches per 1000 carbon atoms.

In an embodiment of the invention, the polyethylene composition (defined as above) is prepared by contacting ethylene and at least one alpha-olefin with a polymerization catalyst under solution phase polymerization conditions in at least two polymerization reactors (for an example of solution phase polymerization conditions see, for example, U.S. Pat. Nos. 6,372,864; 6,984,695 and U.S. Patent Publication Application No. 2006/0247373A1 which are incorporated herein by reference).

In an embodiment of the invention, the polyethylene composition is prepared by contacting at least one single site polymerization catalyst system (comprising at least one single site catalyst and at least one activator) with ethylene and a least one comonomer (e.g., a C3-C8 alpha-olefin) under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the invention, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the invention, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the invention, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal, polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the invention, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the invention, a solution phase dual reactor system comprises two solution phase reactors connected in series.

In an embodiment of the invention, a polymerization process to prepare the polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the invention, a polymerization process to prepare the polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least a first reactor and a second reactor configured in series.

In an embodiment of the invention, a polymerization process to prepare the polyethylene, composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least a first reactor and a second reactor configured in series, with the at least one alpha-olefin comonomer being fed exclusively to the first reactor.

The production of the polyethylene composition of the present invention will typically include an extrusion or compounding step. Such steps are well known in the art.

The polyethylene composition can comprise further polymer components in addition to the first and second ethylene polymers. Such polymer components include polymers made in situ or polymers added to the polymer composition during an extrusion or compounding step.

Optionally, additives can be added to the polyethylene composition. Additives can be added to the polyethylene composition during an extrusion or compounding step, but other suitable known methods will be apparent to a person skilled in the art. The additives can be added as is or as part of a separate polymer component (i.e., not the first or second ethylene polymers described above) added during an extrusion or compounding step. Suitable additives are known in the art and include but are not-limited to antioxidants, phosphites and phosphonites, nitrones, antacids, UV light stabilizers, UV absorbers, metal deactivators, dyes, fillers and reinforcing agents, nano-scale organic or inorganic materials, antistatic agents, lubricating agents such as calcium stearates, slip additives such as erucimide, and nucleating agents (including nucleators, pigments or any other chemicals which may provide a nucleating effect to the polyethylene composition). The additives that can be optionally added are typically added in amount of up to 20 weight percent (wt %).

One or more nucleating agent(s) may be introduced into the polyethylene composition by kneading a mixture of the polymer, usually in powder or pellet form, with the nucleating agent, which may be utilized alone or in the form of a concentrate containing further additives such as stabilizers, pigments, antistatics, UV stabilizers and fillers. It should be a material which is wetted or absorbed by the polymer, which is insoluble in the polymer and of melting point higher than that of the polymer, and it should be homogeneously dispersible in the polymer melt in as fine a form as possible (1 to 10 μm). Compounds known to have a nucleating capacity for polyolefins include salts of aliphatic monobasic or dibasic acids or arylalkyl acids, such as sodium succinate or aluminum phenylacetate; and alkali metal or aluminum salts of aromatic or alicyclic carboxylic acids such as sodium (3-naphthoate. Another compound known to have nucleating capacity is sodium benzoate. The effectiveness of nucleation may be monitored microscopically by observation of the degree of reduction in size of the spherulites into which the crystallites are aggregated.

Examples of nucleating agents which are commercially available and which may be added to the polyethylene composition are dibenzylidene sorbital esters (such as the products sold under the trademark Millad™ 3988 by Milliken Chemical and Irgacleamm by Ciba Specialty Chemicals). Further examples of nucleating agents which may added to the polyethylene composition include the cyclic organic structures disclosed in U.S. Pat. No. 5,981,636 (and salts thereof, such as disodium bicyclo [2.2.1] heptene dicarboxylate); the saturated versions of the structures disclosed in U.S. Pat. No. 5,981,636 (as disclosed in U.S. Pat. No. 6,465,551; Zhao et al., to Milliken); the salts of certain cyclic dicarboxylic acids having a hexahydrophtalic acid structure (or “HHPA” structure) as disclosed in U.S. Pat. No. 6,599,971 (Dotson et al., to Milliken); and phosphate esters, such as those disclosed in U.S. Pat. No. 5,342,868 and those sold under the trade names NA-11 and NA-21 by Asahi Denka Kogyo, cylic dicarboxylates and the salts thereof, such as the divalent metal or metalloid salts, (particularly, calcium salts) of the HHPA structures disclosed in U.S. Pat. No. 6,599,971. For clarity, the HHPA structure generally comprises a ring structure with six carbon atoms in the ring and two carboxylic acid groups which are substituents on adjacent atoms of the ring structure. The other four carbon atoms in the ring may be substituted, as disclosed in U.S. Pat. No. 6,599,971. An example is 1,2-cyclohexanedicarboxylicacid, calcium salt (CAS registry number 491589-22-1). Still further examples of nucleating agents which may added to the polyethylene composition include those disclosed in WO2015042561, WO2015042563, WO2015042562 and WO 2011050042.

Many of the above described nucleating agents may be difficult to mix with the polyethylene composition that is being nucleated and it is known to use dispersion aids, such as for example, zinc stearate, to mitigate this problem.

In an embodiment of the invention, the nucleating agents are well dispersed in the polyethylene composition.

In an embodiment of the invention, the amount of nucleating agent used is comparatively small (from 100 to 3000 parts by million per weight (based on the weight of the polyethylene composition)) so it will be appreciated by those skilled in the art that some care must be taken to ensure that the nucleating agent is well dispersed. In an embodiment of the invention, the nucleating agent is added in finely divided form (less than 50 microns, especially less than 10 microns) to the polyethylene composition to facilitate mixing. This type of “physical blend” (i.e., a mixture of the nucleating agent and the resin in solid form) is generally preferable to the use of a “masterbatch” of the nucleator (where the term “masterbatch” refers to the practice of first melt mixing the additive—the nucleator, in this case—with a small amount of the polyethylene composition resin—then melt mixing the “masterbatch” with the remaining bulk of the polyethylene composition resin).

In an embodiment of the invention, an additive such as nucleating agent may be added to the polyethylene composition by way of a “masterbatch”, where the term “masterbatch” refers to the practice of first melt mixing the additive (e.g., a nucleator) with a small amount of the polyethylene composition, followed by melt mixing the “masterbatch” with the remaining bulk of the polyethylene composition.

In an embodiment of the invention, the polymer composition further comprises a nucleating agent or a mixture of nucleating agents.

In an embodiment of the invention, the polymer compositions described above are used in the formation of molded articles. For example, articles formed by compression molding and injection molding are contemplated. Such articles include, for example, caps, screw caps, and closures for bottles. However, a person skilled in the art will readily appreciate that the compositions described above may also be used for other applications such as, but not limited to, film, injection blow molding, blow molding and sheet extrusion applications.

In an embodiment of the invention, the polyethylene compositions described above are used in the formation of a closure for bottles, containers, pouches and the like. For example, closures for bottles formed by compression molding or injection molding are contemplated. Such closures include, for example, hinged caps, hinged screw caps, hinged snap-top caps, and hinged closures for bottles, containers, pouches and the like.

In an embodiment of the invention, a closure (or cap) is a screw cap for a bottle, container, pouches and the like.

In an embodiment of the invention, a closure (or cap) is a snap closure for a bottle, container, pouches and the like.

In an embodiment of the invention, a closure (or cap) comprises a hinge made of the same material as the rest of the closure (or cap).

In an embodiment of the invention, a closure (or cap) is hinged closure.

In an embodiment of the invention, a closure (or cap) is a hinged closure for bottles, containers, pouches and the like.

In an embodiment of the invention, a closure (or cap) is a flip-top hinge closure, such as a flip-top hinge closure for use on a plastic ketchup bottle or similar containers containing foodstuffs.

When a closure is a hinged closure, it comprises a hinged component and generally consists of at least two bodies which are connected by a thinner section that acts as a hinge allowing the at least two bodies to bend from an initially molded position. The thinner section may be continuous or web-like, wide or narrow.

A useful closure (for bottles, containers and the like) is a hinged closure and may consist of two bodies joined to each other by at least one thinner bendable portion (e.g., the two bodies can be joined by a single bridging portion, or more than one bridging portion, or by a webbed portion, etc.). A first body may contain a dispensing hole and which may snap onto or screw onto a container to cover a container opening (e.g., a bottle opening) while a second body may serve as a snap on lid which may mate with the first body.

The caps and closures, of which hinged caps and closures and screw caps are a subset, can be made according to any known method, including, for example, injection molding and compression molding techniques that are well known to persons skilled in the art. Hence, in an embodiment of the invention a closure (or cap) comprising the polyethylene composition (defined above) is prepared with a process comprising at least one compression molding step and/or at least one injection molding step.

In one embodiment, the caps and closures (including single piece or multi-piece variants and hinged variants) comprise the polyethylene composition described above and have good organoleptic properties, good toughness, as well as good ESCR values. Hence, the closures and caps of this embodiment are well suited for sealing bottles, containers and the like, for example, bottles that may contain drinkable water, and other foodstuffs, including but not limited to liquids that are under an appropriate pressure (i.e., carbonated beverages or appropriately pressurized drinkable liquids).

The closures and caps may also be used for sealing bottles containing drinkable water or non-carbonated beverages (e.g., juice). Other applications, include caps and closures for bottles, containers and pouches containing foodstuffs, such as, for example, ketchup bottles and the like.

The invention is further illustrated by the following non-limiting examples.

EXAMPLES

M_(n), M_(w), and M_(z) (g/mol) were determined by high temperature Gel Permeation Chromatography (GPC) with differential refractive index (DRI) detection using universal calibration (e.g., ASTM-D6474-99). GPC data was obtained using an instrument sold under the trade name “Waters 150c”, with 1,2,4-trichlorobenzene as the mobile phase at 140° C. The samples were prepared by dissolving the polymer in this solvent and were run without filtration. Molecular weights are expressed as polyethylene equivalents with a relative standard deviation of 2.9% for the number average molecular weight (“M_(n)”) and 5.0% for the weight average molecular weight (“M_(w)”). The molecular weight distribution (MWD) is the weight average molecular weight divided by the number average molecular weight, M_(w)/M_(n). The z-average molecular weight distribution is M_(z)/M_(n). Polymer sample solutions (1 to 2 mg/mL) were prepared by heating the polymer in 1,2,4-trichlorobenzene (TCB) and rotating on a wheel for 4 hours at 150° C. in an oven. The antioxidant 2,6-di-tert-butyl-4-methylphenol (BHT) was added to the mixture in order to stabilize the polymer against oxidative degradation. The BHT concentration was 250 ppm. Sample solutions were chromatographed at 140° C. on a PL 220 high-temperature chromatography unit equipped with four Shodex columns (HT803, HT804, HT805 and HT806) using TCB as the mobile phase with a flow rate of 1.0 mL/minute, with a differential refractive index (DRI) as the concentration detector. BHT was added to the mobile phase at a concentration of 250 ppm to protect the columns from oxidative degradation. The sample injection volume was 200 mL. The raw data were processed with Cirrus GPC software. The columns were calibrated with narrow distribution polystyrene standards. The polystyrene molecular weights were converted to polyethylene molecular weights using the Mark-Houwink equation, as described in the ASTM standard test method D6474.

Primary melting peak (° C.), heat of fusion (J/g) and crystallinity (%) was determined using differential scanning calorimetry (DSC) as follows: the instrument was first calibrated with iridium; after the calibration, a polymer specimen is equilibrated at 0° C. and then the temperature was increased to 200° C. at a heating rate of 10° C./min; the melt was then kept isothermally at 200° C. for five minutes; the melt was then cooled to 0° C. at a cooling rate of 10° C./min and kept at 0° C. for five minutes; the specimen was then heated to 200° C. at a heating rate of 10° C./min. The DSC Tm, heat of fusion and crystallinity are reported from the 2^(nd) heating cycle.

The short chain branch frequency (SCB per 1000 carbon atoms) of copolymer samples was determined by Fourier Transform Infrared Spectroscopy (FTIR) as per the ASTM D6645-01 method. A Thermo-Nicolet 750 Magna-IR Spectrophotometer equipped with OMNIC version 7:2a software was used for the measurements.

Comonomer content can also be measured using ¹³C NMR techniques as discussed in Randall, Rev. Macromol. Chem. Phys., C29 (2&3), p. 285; U.S. Pat. No. 5,292,845 and WO 2005/121239.

Polyethylene composition density (g/cm³) was measured according to ASTM D792.

Hexane extractables were determined according to ASTM D5227.

Shear viscosity was measured by using a Kayeness WinKARS Capillary Rheometer (model # D5052M-115). For the shear viscosity at lower shear rates, a die having a die diameter of 0.06 inch and L/D ratio of 20 and an entrance angle of 180 degrees was used. For the shear viscosity at higher shear rates, a die having a die diameter of 0.012 inch and L/D ratio of 20 was used.

The Shear viscosity ratio as the term is used in the present invention is defined as: η₁₀/η₁₀₀₀ at 240° C. The 110 is the melt shear viscosity at the shear rate of 10 s⁻¹ and the η₁₀₀₀ is the melt shear viscosity at the shear rate of 1000 s⁻¹ measured at 240° C.

Melt indexes, I₂, I₅, I₆ and I₂₁ for the polyethylene composition were measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg, a 5 kg, a 6.48 kg and a 21 kg weight, respectively).

To determine CDBI₅₀, a solubility distribution curve is first generated for the polyethylene composition. This is accomplished using data acquired from the TREF technique. This solubility distribution curve is a plot of the weight fraction of the copolymer that is solubilized as a function of temperature. This is converted to a cumulative distribution curve of weight fraction versus comonomer content, from which the CDBI₅₀ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median (See WO 93/03093 and U.S. Pat. No. 5,376,439). The CDBI₂₅ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 25% of the median comonomer content on each side of the median.

The specific temperature rising elution fractionation (TREF) method used herein was as follows. Polymer samples (50 to 150 mg) were introduced into the reactor vessel of a crystallization-TREF unit (Polymer ChAR™). The reactor vessel was filled with 20 to 40 ml 1,2,4-trichlorobenzene (TCB), and heated to the desired dissolution temperature (e.g., 150° C.) for 1 to 3 hours. The solution (0.5 to 1.5 ml) was then loaded into the TREF column filled with stainless steel beads. After equilibration at a given stabilization temperature (e.g., 110° C.) for 30 to 45 minutes, the polymer solution was allowed to crystallize with a temperature drop from the stabilization temperature to 30° C. (0.1 or 0.2° C./minute). After equilibrating at 30° C. for 30 minutes, the crystallized sample was eluted with TCB (0.5 or 0.75 mL/minute) with a temperature ramp from 30° C. to the stabilization temperature (0.25 or 1.0° C./minute). The TREF column was cleaned at the end of the run for 30 minutes at the dissolution temperature. The data were processed using Polymer ChAR software, Excel spreadsheet and TREF software developed in-house.

The melt index, I₂ and density of the first and second ethylene copolymers were estimated by GPC and GPC-FTIR deconvolutions as discussed further below.

High temperature GPC equipped with an online FTIR detector (GPC-FTIR) was used to measure the comonomer content as the function of molecular weight. Mathematical deconvolutions are performed to determine the relative amount of polymer, molecular weight and comonomer content of the component made in each reactor, by assuming that each polymer component follows a Flory's molecular weight distribution function and it has a homogeneous comonomer distribution across the whole molecular weight range.

For these single site catalyzed resins, the GPC data from GPC chromatographs was fit based on Flory's molecular weight distribution function.

To improve the deconvolution accuracy and consistency, as a constraint, the melt index, I₂, of the targeted resin was set and the following relationship was satisfied during the deconvolution: Log₁₀(I ₂)=22.326528+0.003467*[Log₁₀(M _(n))]³−4.322582*Log₁₀(M _(w))−0.180061*[Log₁₀(M _(z))]²+0.026478*[Log₁₀(M _(z))]³ where the experimentally measured overall melt index, I₂, was used on the left side of the equation, while M_(n) of each component (M_(w)=2×M_(n) and M_(z)=1.5×M_(w) for each component) was adjusted to change the calculated overall M_(n), M_(w) and M_(z) of the composition until the fitting criteria were met. During the deconvolution, the overall M_(n), M_(w) and M_(z) are calculated with the following relationships: M_(n)=1/Sum(w_(i)/M_(n)(i)), M_(w)=Sum(w_(i)×M_(w)(i)), M_(z)=Sum(w_(i)×M_(z)(i)²), where i represents the i-th component and w_(i) represents the relative weight fraction of the i-th component in the composition.

The uniform comonomer distribution (which results from the use of a single site catalyst) of the resin components (i.e., the first and second ethylene copolymers) allowed the estimation of the short chain branching content (SCB) from the GPC-FTIR data, in branches per 1000 carbon atoms and calculation of comonomer content (in mol %) and density (in g/cm³) for the first and second ethylene copolymers, based on the deconvoluted relative amounts of first and second ethylene copolymer components in the polyethylene composition, and their estimated resin molecular weight parameters from the above procedure.

A component (or composition) density model and a component (or composition) melt index, I₂, model was used according to the following equations to calculate the density and melt index I₂ of the first and second ethylene polymers: density=0.979863−0.00594808*(FTIR SCB/1000C)^(0.65)−0.000383133*[Log₁₀(M _(n))]³0.00000577986*(M _(w) /M _(n))³+0.00557395*(M _(z) /M _(w))^(0.25); Log₁₀(melt index, I ₂)=22.326528+0.003467*[Log₁₀(M _(n))]³−4.322582*Log₁₀(M _(w))−0.180061*[Log₁₀(M _(z))]²+0.026478*[Log₁₀(M _(z))]³

where the M_(n), M_(w) and M_(z) were the deconvoluted values of the individual ethylene polymer components, as obtained from the results of the above GPC deconvolutions. Hence, these two models were used to estimate the melt indexes and the densities of the components (i.e., the first and second ethylene copolymers).

Plaques molded from the polyethylene compositions were tested according to the following ASTM methods: Bent Strip Environmental Stress Crack Resistance (ESCR) at Condition B at 10% IGEPAL at 50° C., ASTM D1693; notched Izod impact properties, ASTM D256; Flexural Properties, ASTM D 790; Tensile properties, ASTM D 638; Vicat softening point, ASTM D 1525; Heat deflection temperature, ASTM D 648.

Dynamic mechanical analyses were carried out with a rheometer, namely Rheometrics Dynamic Spectrometer (RDS-II) or Rheometrics SR5 or ATS Stresstech, on compression molded samples under nitrogen atmosphere at 190° C., using 25 mm diameter cone and plate geometry. The oscillatory shear experiments were done within the linear viscoelastic range of strain (10% strain) at frequencies from 0.05 to 100 rad/s. The values of storage modulus (G′), loss modulus (G″), complex modulus (G*) and complex viscosity (η*) were obtained as a function of frequency. The same rheological data can also be obtained by using a 25 mm diameter parallel plate geometry at 190° C. under nitrogen atmosphere. The SHI(1,100) value is calculated according to the methods described in WO 2006/048253 and WO 2006/048254.

Examples of the polyethylene compositions were produced in a dual reactor solution polymerization process in which the contents of the first reactor flow into the second reactor. This in-series “dual reactor” process produces an “in-situ” polyethylene blend (i.e., the polyethylene composition). Note, that when an in-series reactor configuration is used, un-reacted ethylene monomer, and un-reacted alpha-olefin comonomer present in the first reactor will flow into the downstream second reactor for further polymerization.

In the present inventive examples, although no co-monomer is fed directly to the downstream second reactor, an ethylene copolymer is nevertheless formed in the second reactor due to the significant presence of un-reacted 1-octene flowing from the first reactor to the second reactor where it is copolymerized with ethylene. Each reactor is sufficiently agitated to give conditions in which components are well mixed. The volume of the first reactor was 12 liters and the volume of the second reactor was 22 liters. Optionally, a tubular reactor section which receives the discharge from the second reactor may be also be present as described in U.S. Pat. No. 8,101,693. These are the pilot plant scales. The first reactor was operated at a pressure of 10500 to 35000 kPa and the second reactor was operated at a lower pressure to facilitate continuous flow from the first reactor to the second. The solvent employed was methylpentane. The process operates using continuous feed streams. The catalyst employed in the dual reactor solution process experiments was a titanium complex having a phosphinimine ligand, a cyclopentadienide ligand and two activatable ligands, such as but not limited to chloride ligands. A boron based co-catalyst was used in approximately stoichiometric amounts relative to the titanium complex. Commercially available methylaluminoxane (MAO) was included as a scavenger at an Al:Ti of about 40:1. In addition, 2,6-di-tert-butylhydroxy-4-ethylbenzene was added to scavenge free trimethylaluminum within the MAO in a ratio of Al:OH of about 0.5:1.

The polymerization conditions used to make the inventive compositions are provided in Table 1.

Inventive and comparative polyethylene composition properties are described in Tables 2.

Calculated properties for the first ethylene copolymer and the second ethylene copolymer for selected comparative and inventive polyethylene compositions, as obtained from GPC-FTIR deconvolution studies, are provided in Table 3.

The properties of pressed plaques made from comparative and inventive polyethylene compositions are provided in Table 4.

Comparative polyethylene compositions (Comparative Examples 1-5) are made using a single site phosphinimine catalyst in a dual reactor solution process and have an ESCR at condition B10 of less than 24 hours and a SCB1/SCB2 ratio of 0.50 or less.

Comparative polyethylene composition 6 (Comparative Example 6) is a commercially available, high density, bimodal polyethylene resin from Dow Chemical, DMDA-1250 NT 7 which has an ESCR at condition B10 (at 50° C., 10% IGEPAL) of less than 200 hours, and an M_(z) of greater than 500,000.

Comparative polyethylene composition 7 (Comparative Example 7) is a commercially available, high density polyethylene resin from Dow Chemical, DMDA-1270 NT 7 which has an ESCR at condition B-10 (at 50° C., 10% IGEPAL) of less than 100 hours, and an M_(z) of greater than 450,000.

Inventive polyethylene compositions 1-9 (Inventive Examples 1-9) are made using a single site phosphinimine catalyst in a dual reactor solution process as described above and have an ESCR at condition B10 of greater than 20 hours and a SCB1/SCB2 ratio of greater than 0.50. These inventive examples also have a M_(z) values of less than 400,000.

Inventive polyethylene compositions 10-13 (Inventive Examples 10-13) are made using a single site phosphinimine catalyst in a dual reactor solution process as described above and have an ESCR at condition B10 of greater than 250 hours and a SCB1/SCB2 ratio of greater than 1.5. These inventive examples also have a M_(z) values of less than 450,000.

TABLE 1 Reactor Conditions for Inventive Examples Inventive Inventive Inventive Inventive Inventive Example Example Example Example Example Example No. 1 2 3 4 5 Reactor 1 Ethylene (kg/h) 35.6 38.1 35.7 36.7 37.5 1-Octene (kg/h) 4.9 4 5.3 4.1 4.8 Hydrogen (g/h) 0.51 0.58 0.51 0.50 0.50 Solvent (kg/h) 319.2 329 296.5 296.8 286.8 Reactor Feed Inlet 30 30 30 30 30 Temperature (° C.) Reactor 138.2 140.5 141.1 143.8 149.2 Temperature (° C.) Titanium Catalyst to 0.14 0.10 0.12 0.1 0.1 the Reactor (ppm) Reactor 2 Ethylene (kg/h) 43.6 51.6 43.6 44.9 45.9 1-Octene (kg/h) 0 0 0 0 0 Hydrogen (g/h) 22.2 13.46 22.2 16.4 21 Solvent (kg/h) 106.7 137.2 129.1 127.5 135 Reactor Feed Inlet 30 30 30 31.3 29.8 Temperature (° C.) Reactor 186.9 192.1 186.3 190.9 194 Temperature (° C.) Titanium Catalyst to 0.29 0.23 0.21 0.21 0.24 the Reactor (ppm) Example Inventive Inventive Inventive Inventive No. Example 6 Example 7 Example 8 Example 9 Reactor 1 Ethylene (kg/h) 35.7 35.6 35.7 38.4 1-Octene (kg/h) 2.6 4.7 4.9 1.5 Hydrogen (g/h) 0.45 0.46 0.46 0.62 Solvent (kg/h) 256.6 259.1 258.9 346.3 Reactor Feed Inlet 30 30 30 30 Temperature (° C.) Reactor 152.5 151 147 141.1 Temperature (° C.) Titanium Catalyst to 0.08 0.13 0.10 0.10 the Reactor (ppm) Reactor 2 Ethylene (kg/h) 43.6 43.6 43.6 51.9 1-Octene (kg/h) 0 0 0 0 Hydrogen (g/h) 10.2 21.59 16.21 15.07 Solvent (kg/h) 171.6 167 167.1 121.7 Reactor Feed Inlet 30 30 30 30 Temperature (° C.) Reactor 185.7 186.2 186.4 192.8 Temperature (° C.) Titanium Catalyst to 0.13 0.22 0.20 0.31 the Reactor (ppm) Example Inventive Inventive Inventive Inventive No. Example 10 Example 11 Example 12 Example 13 Reactor 1 Ethylene (kg/h) 34.1 34.1 34.1 32.6 1-Octene (kg/h) 4 3.1 4.8 4.9 Hydrogen (g/h) 0.27 0.22 0.35 0.29 Solvent (kg/h) 331.3 345.1 314.4 311.4 Reactor Feed Inlet 30 30 30 30 Temperature (° C.) Reactor 135.8 137 139.9 140 Temperature (° C.) Titanium Catalyst to 0.08 0.13 0.09 0.13 the Reactor (ppm) Reactor 2 Ethylene (kg/h) 41.7 41.7 41.7 40.0 1-Octene (kg/h) 0 0 0 0 Hydrogen (g/h) 19.8 19.25 23.10 20.35 Solvent (kg/h) 128.8 115.7 144.9 151.1 Reactor Feed Inlet 29.8 34.2 30 30.5 Temperature (° C.) Reactor 192.2 192 191.9 186.3 Temperature (° C.) Titanium Catalyst to 0.29 0.21 0.28 0.21 the Reactor (ppm)

TABLE 2 Resin Properties Comparative Comparative Comparative Comparative Comparative Example No. Example 1 Example 2 Example 3 Example 4 Example 5 Density (g/cm³) 0.9534 0.9523 0.9526 0.952 0.953 Rheology/Flow Properties Melt Index I₂ 1.88 0.625 1.42 1.92 0.68 (g/10 min) Melt Flow Ratio 56.9 51.2 50.5 77.1 73.2 (I₂₁/I₂) Stress Exponent 1.41 1.38 1.36 1.38 1.38 I₂₁ (g/10 min) 107 33.1 71.3 146.0 49.8 I₅ (g/10 min) 4.23 I₂₁/I₅ 16.86 Shear Viscosity 5.8 at 10⁵ s⁻¹ (240° C., Pa-s) Shear Viscosity 12.0 Ratio η(10 s⁻¹)/η(1000 s⁻¹) at 240° C. DMA Data η* = 5832 (190° C.) Pa * s at G* = 2.099 kPa; η* = 5591 Pa * s at G* = 2.795 kPa GPC M_(n) 14393 22392 17827 9891 12424 M_(w) 91663 109626 105289 77319 104353 M_(z) 325841 299470 282159 245479 327007 Polydispersity 6.37 4.9 5.91 7.82 8.4 Index (M_(w)/M_(n)) M_(z)/M_(w) 3.55 3.56 2.68 3.17 3.13 Broadness Factor 1.79 1.38 2.21 2.47 2.68 (M_(w)/M_(n))/(M_(z)/M_(w)) Branch Frequency - FTIR (uncorrected for chain end —CH₃) Uncorrected 2.2 2 2.2 3.7 2.5 SCB/1000 C Uncorrected 0.4 0.4 0.4 0.7 0.5 comonomer content (mol %) Comonomer ID 1-octene 1-octene 1-octene 1-octene 1-octene Comonomer mol % measured by ¹³C-NMR Hexyl+ branches 0.3 0.2 0.28 (≥4 carbon atoms), mol % Slow-CTREF CDBI₅₀ (wt. %) 63 CDBI₂₅ (wt. %) DSC Primary Melting 128.3 129.7 129.11 126.8 128.42 Peak (° C.) Heat of Fusion 204.7 198.2 207.7 200.3 213.80 (J/g) Crystallinity (%) 70.58 68.34 71.61 69.08 73.72 Other properties Hexane 0.44 0.46 0.32 0.73 0.57 Extractables (wt %) VICAT Soft. Pt. 126 127 127.3 122 125 (° C.) - Plaque Heat Deflection 72 71 68.2 68 71 Temp. [° C.] @ 66 PSI Comparative Comparative Inventive Inventive Inventive Example No. Example 6 Example 7 Example 1 Example 2 Example 3 Density (g/cm³) 0.955 0.955 0.9529 0.9524 0.9524 Rheology/Flow Properties Melt Index I₂ 1.5 2.5 1.57 2.94 1.69 (g/10 min) Melt Flow Ratio 66 51 58 44.1 61 (I₂₁/I₂) Stress Exponent 1.58 1.53 1.38 1.36 1.38 I₂₁ (g/10 min) 99 113 90 129 104 I₅ (g/10 min) 5.31 7.8 4.72 4.94 I₂₁/I₅ 18.64 19.07 21.05 Shear Viscosity 6.2 6.63 5.1 6.2 4.8 at 10⁵ s⁻¹ (240° C., Pa-s) Shear Viscosity 11.3 9.48 13.5 8.1 13.0 Ratio η(10 s⁻¹)/η(1000 s⁻¹) at 240° C. DMA Data η* = 5294 η* = 4889 (190° C.) Pa * s at G* = Pa * s at G* = 2.647 kPa; 2.445 kPa; η* = 5106 η* = 4739 Pa * s at G* = Pa * s at G* = 3.547 kPa 3.292 kPa GPC M_(n) 10240 17100 10524 15679 10579 M_(w) 106992 102000 83712 74090 86319 M_(z) 533971 470400 256210 215369 291056 Polydispersity 10.45 5.96 7.95 4.73 8.16 Index (M_(w)/M_(n)) M_(z)/M_(w) 4.99 4.61 3.06 2.91 3.37 Broadness Factor 2.09 1.29 2.60 1.63 2.42 (M_(w)/M_(n))/(M_(z)/M_(w)) Branch Frequency - FTIR (uncorrected for chain end —CH₃) Uncorrected 2.3 2.5 3 1.8 3 SCB/1000 C Uncorrected 0.5 0.5 0.6 0.4 0.6 comonomer content (mol %) Comonomer ID 1-hexene 1 -hexene 1-octene 1-octene 1-octene Comonomer mol % measured by ¹³C-NMR Hexyl+ branches 0.68 0.4 0.4 (≥4 carbon atoms), mol % Slow-CTREF CDBI₅₀ (wt. %) 63.4 67.3 CDBI₂₅ (wt. %) 39 49.8 65.4 61.8 61.8 DSC Primary Melting 130.06 131.24 127.3 128.8 127.5 Peak (° C.) Heat of Fusion 217.4 217.6 203.8 206.1 207.3 (J/g) Crystallinity (%) 74.98 75.04 70.27 71.08 71.48 Other properties Hexane 0.36 0.48 0.36 0.22 0.42 Extractables (wt %) VICAT Soft. Pt. 126.8 126.6 125.2 126.8 124.8 (° C.) - Plaque Heat Deflection 73 76.4 68 74.1 76 Temp. [° C.] @ 66 PSI Inventive Inventive Inventive Inventive Inventive Example No. Example 4 Example 5 Example 6 Example 7 Example 8 Density (g/cm³) 0.9523 0.9532 0.9527 0.9534 0.9522 Rheology/Flow Properties Melt Index I₂ 1.5 1.78 1.29 2.05 1.31 (g/10 min) Melt Flow Ratio 54.8 55.6 44.1 55 64 (I₂₁/I₂) Stress Exponent 1.4 1.37 1.35 1.34 1.39 I₂₁ (g/10 min) 82.3 99.1 57 113 83 I₅ (g/10 min) 4.5 5.33 6.21 I₂₁/I₅ 18.29 18.59 18.20 Shear Viscosity 5.8 5.1 6.3 5.0 5.8 at 10⁵ s⁻¹ (240° C., Pa-s) Shear Viscosity 14.8 13.3 11.6 12.1 14.8 Ratio η(10 s⁻¹)/η(1000 s⁻¹) at 240° C. DMA Data η* = 6707 η* = 6688 (190° C.) Pa * s at G* = Pa * s at G* = 2.413 kPa; 2.407 kPa; η* = 6465 η* = 6472 Pa * s at G* = Pa * s at G* = 3.232 kPa 3.236 kPa GPC M_(n) 13309 9716 18449 11145 14021 M_(w) 88295 84943 93080 80630 93175 M_(z) 278141 288665 272788 243944 303823 Polydispersity 6.63 8.74 5.05 7.23 6.65 Index (M_(w)/M_(n)) M_(z)/M_(w) 3.15 3.40 2.93 3.03 3.26 Broadness Factor 2.10 2.57 1.72 1.43 2.04 (M_(w)/M_(n))/(M_(z)/M_(w)) Branch Frequency - FTIR (uncorrected for chain end —CH₃) Uncorrected 2.1 2.5 1.7 2.8 2.2 SCB/1000 C Uncorrected 0.4 0.5 0.3 0.6 0.4 comonomer content (mol %) Comonomer ID 1-octene 1-octene 1-octene 1-octene 1-octene Comonomer mol % measured by ¹³C-NMR Hexyl+ branches 0.3 (>= 4 carbon atoms), mol % Slow-CTREF CDBI₅₀ (wt. %) 76.5 75.2 86.2 79.7 80.4 CDBI₂₅ (wt. %) DSC Primary Melting 129 128.3 129.8 127.9 128.4 Peak (° C.) Heat of Fusion 209 207.3 208.5 211.1 205.4 (J/g) Crystallinity (%) 72.08 71.48 71.9 72.8 70.82 Other properties Hexane 0.25 0.33 0.25 0.38 0.27 Extractables (wt %) VICAT Soft. Pt. 126.4 125.4 128.2 125.2 126.2 (° C.) - Plaque Heat Deflection 67.3 69.8 68.2 66.8 69 Temp. [° C.] @ 66 PSI Inventive Inventive Inventive Inventive Inventive Example No. Example 9 Example 10 Example 11 Example 12 Example 13 Density (g/cm³) 0.9568 0.9545 0.9532 0.9543 0.9522 Rheology/Flow Properties Melt Index I₂ 1.68 0.67 0.76 1.15 1.35 (g/10 min) Melt Flow Ratio 54.2 53 48.3 84 88 (I₂₁/I₂) Stress Exponent 1.40 1.38 1.39 1.39 1.38 I₂₁ (g/10 min) 91 53 48.3 84 88 I₅ (g/10 min) 2.14 2.36 3.54 4.12 I₆ (g/10 min) 3.07 3.5 5.29 6.18 I₂₁/I₅ 24.77 20.47 23.73 21.36 Shear Viscosity 6.0 4.8 5.1 4.4 4.6 at 10⁵ s⁻¹ (240° C., Pa-s) Shear Viscosity 11.2 22.3 19.1 17.9 14.6 Ratio η(10 s⁻¹)/η(1000 s⁻¹) at 240° C. DMA Data (190° C.) GPC M_(n) 15110 10953 10876 9202 9424 M_(w) 85227 112697 112804 98160 86829 M_(z) 287035 388883 375939 332900 286320 Polydispersity 5.64 10.29 10.37 10.67 9.21 Index (M_(w)/M_(n)) M_(z)/M_(w) 3.37 3.45 3.33 3.39 3.30 Broadness Factor 1.67 2.98 3.11 3.15. 2.79 (M_(w)/M_(n))/(M_(z)/M_(w)) Branch Frequency - FTIR (uncorrected for chain end —CH₃) Uncorrected 1.3 2.5 2.5 2.9 3.2 SCB/1000 C Uncorrected 0.3 0.5 0.5 0.6 0.6 comonomer content (mol %) Comonomer ID 1 -octene 1-octene 1-octene 1-octene 1-octene Comonomer mol % measured by ¹³C-NMR Hexyl+ branches (>= 4 carbon atoms), mol % Slow-CTREF CDBI₅₀ (wt. %) 77.8 73 75.7 71.9 77.3 CDBI₂₅ (wt. %) 64.4 66.5 64.1 69.4 DSC Primary Melting 130.7 128.76 128.69 128.29 127.52 Peak (° C.) Heat of Fusion 213.8 221.5 217.1 218.8 215.2 (J/g) Crystallinity (%) 73.73 76.39 74.86 75.45 74.22 Other properties Hexane 0.24 0.40 0.30 0.53 0.46 Extractables (wt %) VICAT Soft. Pt. 128.4 126.1 126.2 125.6 124.7 (° C.) - Plaque Heat Deflection 77.6 78 74.6 75.7 67.4 Temp. [° C.] @ 66 PSI

TABLE 3 Polyethylene Component Properties (Comparative Examples) Comparative Comparative Comparative Comparative Comparative Example No. Example 1 Example 2 Example 3 Example 4 Example 5 Density (g/cm³) 0.9534 0.9523 0.9526 0.952 0.953 I₂ (g/10 min.) 1.88 0.625 1.42 1.92 0.68 Stress Exponent 1.41 1.38 1.36 1.38 1.38 MFR (I₂₁/I₂) 56.9 51.2 50.5 77.1 73.2 Mw/Mn 6.37 4.9 6.34 7.82 8.39 1^(st) Ethylene Copolymer weight % 0.43 0.43 0.433 0.426 0.449 Mw 162400 214300 176200 169500 213200 I₂ (g/10 min.) 0.13 0.05 0.10 0.11 0.05 Density 1, d₁ 0.9389 0.9356 0.9334 0.9382 0.9363 (g/cm³) SCB1 per 0.15 0.13 1.07 0.18 0.06 1000 Cs mol % 1-octene 0.03 0.03 0.21 0.04 0.01 2^(nd) Ethylene Copolymer weight % 0.57 0.57 0.567 0.574 0.551 Mw 18500 25600 17300 11700 14300 I₂ (g/10 min.) 736 190 979 5082 2148 Density 2, d₂ 0.9559 0.9522 0.9528 0.9559 0.9565 (g/cm³) SCB2 per 1.06 1.37 2.16 2.1 1.42 1000 Cs mol % 1-octene 0.21 0.27 0.43 0.42 0.28 Estimated 0.017 0.0166 0.0194 0.0177 0.0202 (d₂ − d₁), g/cm³ Estimated 0.91 1.24 1.09 1.92 1.36 (SCB2 − SCB1) SCB1/SCB2 0.14 0.09 0.50 0.09 0.04 Inventive Inventive Inventive Inventive Example No. Example 3 Example 4 Example 5 Example 7 Density (g/cm³) 0.9524 0.9523 0.9532 0.9534 I₂ (g/10 min.) 1.69 1.5 1.78 2.05 Stress Exponent 1.38 1.4 1.37 1.34 MFR (I₂₁/I₂) 61 54.8 55.6 55 Mw/Mn 8.16 6.63 8.74 7.23 1^(st) Ethylene Copolymer weight % 0.455 0.454 0.454 0.453 Mw 165100 168100 162700 157200 I₂ (g/10 min.) 0.13 0.12 0.13 0.15 Density 1, d₁ 0.9325 0.9302 0.9322 0.9316 (g/cm³) SCB1 per 1.57 2.24 1.71 2.02 1000 Cs mol % 1-octene 0.31 0.45 0.34 0.40 2^(nd) Ethylene Copolymer weight % 0.545 0.546 0.546 0.547 Mw 11100 14900 12100 11400 I₂ (g/10 min.) 6318 1817 4419 5739 Density 2, d₂ 0.9614 0.9555 0.959 0.9577 (g/cm³) SCB2 per 0.63 1.64 1.08 1.59 1000 Cs mol % 1-octene 0.13 0.33 0.22 0.32 Estimated 0.0289 0.0253 0.0268 0.0261 (d₂ − d₁), g/cm³ Estimated −0.94 −0.6 −0.63 −0.43 (SCB2 − SCB1) SCB1/SCB2 2.5 1.37 1.58 1.27 Inventive Inventive Inventive Inventive Example No. Example 10 Example 11 Example 12 Example 13 Density (g/cm³) 0.9545 0.9532 0.9543 0.9522 I₂ (g/10 min.) 0.67 0.76 1.15 1.35 Stress Exponent 1.38 1.39 1.39 1.38 MFR (I₂₁/I₂) 79 64 73 64 Mw/Mn 10.29 10.37 10.67 9.21 1^(st) Ethylene Copolymer weight % 0.429 0.464 0.423 0.433 Mw 226800 201800 199000 185900 I₂ (g/10 min.) 0.04 0.06 0.06 0.08 Density 1, d₁ 0.9295 0.9299 0.9312 0.9318 (g/cm³) SCB1 per 1.3 1.6 1.28 1.35 1000 Cs mol % 1-octene 0.26 0.32 0.26 0.27 2^(nd) Ethylene Copolymer weight % 0.571 0.536 0.577 0.567 Mw 10900 11200 9300 10000 I₂ (g/10 min.) 6980 6163 13434 10206 Density 2, d₂ 0.9643 0.9631 0.9639 0.9640 (g/cm³) SCB2 per 0.15 0.29 0.38 0.29 1000 Cs mol % 1-octene 0.03 0.06 0.08 0.06 Estimated 0.0348 0.0332 0.0327 0.0322 (d₂ − d₁), g/cm³ SCB1/SCB2 8.67 5.52 3.37 4.66

TABLE 4 Plaque Properties Comparative Comparative Comparative Comparative Comparative Example No. Example 1 Example 2 Example 3 Example 4 Example 5 Environmental Stress Crack Resistance ESCR Cond. B <24 <24 <24 <24 <24 at 10% (hours) Flexural Properties (Plaques) Flex Secant Mod. 1035 1070 1198 1062 1201 1% (MPa) Flex Sec Mod 1% 25 37 38 34 41 (MPa) Dev. Flex Secant Mod. 877 906 1011 904 1002 2% (MPa) Flex Sec Mod 2% 19 29 22 28 32 (MPa) Dev. Flexural Strength 31.5 33.4 35.1 33 35.5 (MPa) Flexural Strength 0.6 0.7 0.4 0.9 0.6 Dev. (MPa) Tensile Properties (Plaques) Elong. at Yield 10.2 10.3 10 10.3 10.2 (%) Elong. at Yield 0.8 1 0 0.3 0.4 Dev. (%) Yield Strength 26.6 25.4 26.3 25.7 26.9 (MPa) Yield Strength 0.3 0.4 0.6 0.6 0.3 Dev. (MPa) Ultimate Elong. 920 1003 858 535 800 (%) Ultimate Elong. 94.6 23.7 37 167.4 86.1 Dev. (%) Ultimate Strength 21.5 33.8 21.4 14.8 20.7 (MPa) Ultimate Strength 4.1 1.1 1.8 0.7 6.7 Dev. (MPa) Sec Mod 1% 1374 1138 1294 1244 1237 (MPa) Sec Mod 1% 276.4 210.8 188 47.1 83 (MPa) Dev. Sec Mod 2% 937 834 900 858 888 (MPa) Sec Mod 2% 71 61 44 24 47 (MPa) Dev. Impact Properties (Plagues) Notched Izod 76 139 64.1 69.4 97.1 Impact (J/m) IZOD DV (J/m) 7 7 5.3 6.9 2.8 Comparative Comparative Inventive Inventive Inventive Example No. Example 6 Example 7 Example 1 Example 2 Example 3 Environmental Stress Crack Resistance ESCR Cond. B 196 78 309 23 212 at 10% (hours) Flexural Properties (Plaques) Flex Secant Mod. 1372 1304 1274 1247 1267 1% (MPa) Flex Sec Mod 1% 87 46 39 44 19 (MPa) Dev. Flex Secant Mod. 1167 1102 1064 1035 1060 2% (MPa) Flex Sec Mod 2% 45 41 29 33 14 (MPa) Dev. Flexural Strength 40.4 38.3 37.5 36.7 37.1 (MPa) Flexural Strength 1 0.6 0.8 0.4 0.3 Dev. (MPa) Tensile Properties (Plaques) Elong. at Yield 9 9 9 10 8 (%) Elong. at Yield 1 1 1 1 0 Dev. (%) Yield Strength 28.5 26.4 26 25.6 26.4 (MPa) Yield Strength 0.3 0.3 0.2 0.1 0.3 Dev. (MPa) Ultimate Elong. 870 1055 701 988 762 (%) Ultimate Elong. 69 42 106 58 98 Dev. (%) Ultimate Strength 26.8 31.6 21.8 32.2 24.7 (MPa) Ultimate Strength 5.5 1 6.8 1.9 7.4 Dev. (MPa) Sec Mod 1% 1696 1545 1483 1256 1331 (MPa) Sec Mod 1% 279 231 121 333 241 (MPa) Dev. Sec Mod 2% 1118 993 973 880 939 (MPa) Sec Mod 2% 90 91 33 88 62 (MPa) Dev. Impact Properties (Plagues) Notched Izod 80.1 80 74.7 69.4 69.4 Impact (J/m) IZOD DV (J/m) 5.3 0.0 0.0 0.0 Inventive Inventive Inventive Inventive Inventive Example No. Example 4 Example 5 Example 6 Example 7 Example 8 Environmental Stress Crack Resistance ESCR Cond. B 86 83 60 73 157 at 10% (hours) Flexural Properties (Plaques) Flex Secant Mod. 1295 1304 1240 1318 1260 1% (MPa) Flex Sec Mod 1% 23 57 31 37 25 (MPa) Dev. Flex Secant Mod. 1085 1092 1026 1098 1049 2% (MPa) Flex Sec Mod 2% 21 40 26 24 15 (MPa) Dev. Flexural Strength 37.3 37.6 36.1 38.2 36.9 (MPa) Flexural Strength 0.4 0.8 0.6 0.3 0.6 Dev. (MPa) Tensile Properties (Plaques) Elong. at Yield 10 9 10 8 9 (%) Elong. at Yield 0 0 0 0 1 Dev. (%) Yield Strength 26.3 26.4 25.6 26.9 26.1 (MPa) Yield Strength 0.3 0.2 0.2 0.2 0.2 Dev. (MPa) Ultimate Elong. 891 862 974 766 836 (%) Ultimate Elong. 23 47 35 130 103 Dev. (%) Ultimate Strength 33.3 29.7 36.3 22.9 29.6 (MPa) Ultimate Strength 2 2.7 1.5 7 5.5 Dev. (MPa) Sec Mod 1% 1230 1197 1333 1429 1395 (MPa) Sec Mod 1% 90 128 213 183 217 (MPa) Dev. Sec Mod 2% 913 881 893 979 934 (MPa) Sec Mod 2% 34 40 70 52 73 (MPa) Dev. Impact Properties (Plagues) Notched Izod 80.1 64.1 128.1 64.1 80.1 Impact (J/m) IZOD DV (J/m) 2.7 2.1 5.3 0.0 0.0 Inventive Inventive Inventive Inventive Inventive Example No. Example 9 Example 10 Example 11 Example 12 Example 13 Environmental Stress Crack Resistance ESCR Cond. B 24 1100 720 399 to 484 655 at 10% (hours) Flexural Properties (Plaques) Flex Secant Mod. 1402 1341 1330 1354 1297 1% (MPa) Flex Sec Mod 1% 48 34 30 34 27 (MPa) Dev. Flex Secant Mod. 1159 1131 1119 1138 1095 2% (MPa) Flex Sec Mod 2% 35 26 22 26 16 (MPa) Dev. Flexural Strength 39.8 39.1 38.4 38.7 38.1 (MPa) Flexural Strength 1.1 0.4 0.5 0.4 0.6 Dev. (MPa) Tensile Properties (Plaques) Elong. at Yield 10 9 8 8 9 (%) Elong. at Yield 0 1 1 1 1 Dev. (%) Yield Strength 28.2 27.2 26.9 27.7 26.1 (MPa) Yield Strength 0.6 0.5 0.4 0.5 0.5 Dev. (MPa) Ultimate Elong. 923 810 821 747 694 (%) Ultimate Elong. 104 73 103 94 95 Dev. (%) Ultimate Strength 26.9 33 33.2 24.3 23 (MPa) Ultimate Strength 6.9 5.7 8.4 7.4 6.9 Dev. (MPa) Sec Mod 1% 1367 1586 1624 1506 1358 (MPa) Sec Mod 1% 190 258 323 369 207 (MPa) Dev. Sec Mod 2% 966 1031 1031 1034 950 (MPa) Sec Mod 2% 67 65 97 113 48 (MPa) Dev. Impact Properties (Plagues) Notched Izod 90.7 107.0 107.0 69.4 80.0 Impact (J/m) IZOD DV (J/m) 5.3 5.3 5.3 0.0 5.3

As can be seen from the data provided in Tables 2, 3 and 4, the Inventive polyethylene compositions (Inventive Examples 1-9) which have a ratio of short chain branching SCB1/SCB2 of greater than 0.5, have improved ESCR B properties while maintaining good processability.

As shown in FIG. 1, inventive polyethylene compositions 1, 10, 11 and 13 provide an improved balance of ESCR and stiffness (as indicated by 2% secant floral modulus) when compared to comparative polyethylene compositions 6, and 7.

As shown in FIG. 2, inventive polyethylene compositions 1, 10, 11 and 13 provide an improved balance of ESCR and processability (as indicated by the “shear viscosity ratio”) when compared to comparative polyethylene compositions 6 and 7.

As shown in FIG. 3, inventive polyethylene compositions 1, 10, 11 and 13 provide an improved balance of processability (as indicated by the “shear viscosity ratio”) and Notched Izod Impact Strength, when compared to comparative polyethylene compositions 6 and 7.

FIG. 4 shows that inventive polyethylene compositions 1, 10, 11 and 13 have an improved balance of processability (as indicated by the “shear viscosity ratio”) and stiffness (as indicated by 2% secant floral modulus) when compared to comparative polyethylene compositions 6, and 7.

As shown in FIG. 5, the inventive polyethylene compositions 1, 3, 5, 6 and 8 do not satisfy the equation SHI(1, 100) 2-10.58 (log I₂ of the polyethylene composition in g/10 min)/(g/10 min)+12.94, which is a property of the blends taught in WO 2006/048253. As shown in FIG. 5, the inventive polyethylene compositions 1, 3, 5, 6 and 8 do not satisfy the equation: SHI_((1,100))≥−5.5(log I ₂ of the polyethylene composition in g/10 min)/(g/10 min)+9.66, which is a property of the blends taught in and WO 2006/048254.

FIG. 6 shows the bimodal nature of the inventive polyethylene compositions 10-13. Each ethylene copolymer component has a M_(w)/M_(n) value of less than 2.5.

As shown in FIG. 7, the inventive polyethylene compositions 10-13 do not satisfy the equation SHI_((1, 100))≥−10.58 (log I₂ of the polyethylene composition in g/10 min)/(g/10 min)+12.94, which is a property of the blends taught in WO 2006/048253. As shown in FIG. 7, the inventive polyethylene compositions 10-13 do not satisfy the equation: SHI_((1,100))≥−5.5 (log I₂ of the polyethylene composition in g/10 min)/(g/10 min)+9.66, which is a property of the blends taught in and WO 2006/048254. 

What is claimed is:
 1. A closure for bottles, said closure comprising a bimodal polyethylene composition comprising: (1) 10 to 70 wt % of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.920 to 0.955 g/cm³; and (2) 90 to 30 wt % of a second ethylene copolymer having a melt index I₂, of from 100 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of said first ethylene copolymer, but less than 0.967 g/cm³; wherein the density of said second ethylene copolymer is less than 0.037 g/cm³ higher than the density of said first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in said first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in said second ethylene copolymer (SCB2) is greater than 0.5; and wherein said bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3 to 11; a density of at least 0.949 g/cm³; a melt index I₂, of from 0.4 to 5.0 g/10 min; an M_(z) of less than 400,000; a stress exponent of less than 1.50; and an ESCR Condition B (10% IGEPAL) of from 60 to 400 hrs.
 2. The closure of claim 1 wherein the bimodal polyethylene composition further comprises a nucleating agent.
 3. The closure of claim 1 wherein said closure is made by compression molding or injection molding. 